US6739383B1 - Method for continuously casting between two rolls austenitic stainless steel strips with excellent surface quality and resulting strips - Google Patents

Method for continuously casting between two rolls austenitic stainless steel strips with excellent surface quality and resulting strips Download PDF

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US6739383B1
US6739383B1 US09/959,210 US95921002A US6739383B1 US 6739383 B1 US6739383 B1 US 6739383B1 US 95921002 A US95921002 A US 95921002A US 6739383 B1 US6739383 B1 US 6739383B1
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rolls
steel
strip
gas
microcracks
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Christian Marchionni
Frédéric Mazurier
Jean-Michel Damasse
Frédéric Descaves
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USINOR SA
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USINOR SA
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
    • B22D11/0637—Accessories therefor
    • B22D11/0648—Casting surfaces
    • B22D11/0651—Casting wheels
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
    • B22D11/002—Stainless steels
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
    • B22D11/0622—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
    • B22D11/0637—Accessories therefor
    • B22D11/0697—Accessories therefor for casting in a protected atmosphere
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel

Definitions

  • the invention relates to the continuous casting of metals, and more specifically to the continuous casting, directly from liquid metal, of austenitic-type stainless steel strip whose thickness is of the order of a few mm, using the process called “twin-roll casting”.
  • the process mainly used at the present time is that of casting said liquid metal between two internally cooled rolls, rotating about their horizontal axes in opposite directions and placed opposite one another, the minimum distance between their surfaces being approximately equal to the thickness that it is desired to give the cast strip (for example, a few mm).
  • the casting space containing the liquid steel is defined by the lateral surfaces of the rolls, on which the strip starts to solidify, and by lateral closure plates made of refractory which are applied against the ends of the rolls.
  • the liquid metal starts to solidify on contact with the external surfaces of the rolls, on which it forms solidified “shells”, arrangements being made for the shells to join together in the “nip”, that is to say the region where the distance between the rolls is a minimum.
  • microcracks form during solidification of the steel and have a depth of about 40 ⁇ m and an opening of approximately 20 ⁇ m. Their appearance depends on the contractions of the metal, during solidification of the shells on contact with the rolls over the length of their contact arc. This solidification may be described as having two successive steps. The first step takes place during the initial contact between the liquid steel and the surface of the roll, which results in the formation of a solid steel shell at the surface of the rolls.
  • the second step relates to the growth of this shell as far as the nip, where, as mentioned, it joins the shell formed on the other roll in order to constitute the fully solidified strip.
  • the contact between the steel and the surface of the roll is determined by the topography of the surface of the casting rolls, together with the nature of the inert gas surrounding the casting space and the chemical composition of the steel. All these parameters are involved in establishing the heat transfer between the steel and the roll and govern the conditions under which the shells solidify. As the shells solidify and cool, they undergo contractions. These depend especially on the extent of the ⁇ phase transformation, which takes place with a substantial change in the density of the metal, at the microscopic level. It is determined by the composition of the cast metal. These contractions will also modify the shell solidification and cooling conditions.
  • the Cr eq /Ni eq ratio is conventionally considered as being representative of the solidification path of austenitic stainless steels. It is calculated, using the Hammar and Swensson relationship, by means of the formulae (the percentages are weight percentages):
  • Ni eq (%) Ni%+0.31Mn%+22C%+14.2N%+Cu%.
  • the dimples may conventionally be produced by shot blasting or laser machining. In both the above documents, there is a requirement for these dimples to be separated from one another.
  • EP-A-0 679 114 proposes the use of circumferential grooves made on the surface of the rolls, which give said surface a roughness Ra of 2.5 to 15 ⁇ m. It is combined with a chemical composition of the steel allowing solidification as primary austenite, characterized by a Cr eq /Ni eq ratio of less than 1.60. However, solidification as primary austenite increases the hot cracking sensitivity of stainless steels and the risks of forming longitudinal cracks in the strip.
  • the document EP-A-0 796 685 teaches the casting of a steel whose Cr eq /Ni eq ratio is greater than 1.55 so as to minimize the phase changes at high temperature and to carry out this casting by using rolls whose surface includes touching dimples 100-1500 ⁇ m in diameter and 20-150 ⁇ m in depth and by inerting the region around the meniscus (the intersection between the surface of the liquid steel and the surface of the rolls) with a gas soluble in the steel, or a gas mixture composed predominantly of such a soluble gas.
  • the roughness peaks serve as sites for initiating the solidification, whereas the valleys of the roughness constitute metal contraction joints during solidification, and allow better distribution of the stresses.
  • the CR eq /Ni eq ratio is greater than 1.70, it is not always possible to avoid the presence of a few microcracks.
  • the composition of said steel in percentages by weight, comprises: C % ⁇ 0.08; Si % ⁇ 1; P % ⁇ 0.04; Mn % ⁇ 2; Cr % between 17 and 20; Ni % between 8 and 10.5; S % between 0.007 and 0.040; the balance being iron and impurities resulting from the smelting;
  • Ni eq (%) Ni%+0.31Mn%+22C%+14.2N%+Cu%;
  • the surface of the rolls has touching dimples of approximately circular or elliptical cross section, having a diameter of 100 to 1500 ⁇ m and a depth of 20 to 150 ⁇ m;
  • the inert gas surrounding the meniscus is a gas soluble in the steel or a mixture of such gases, or consists of at least 50% by volume of such a gas or gas mixture.
  • the subject of the invention is also strip that can be produced by this process.
  • the invention consists in combining conditions relating to the composition of the cast metal, the surface finish of the rolls and the composition of the gas for inerting the meniscus, so as to obtain a strip surface free of microcracks.
  • the main novelty of the composition required is that the metal must contain an amount of sulfur greater than the amounts more usually encountered (without, however, being high to the point of compromising the corrosion resistance of the products) and that this content must be combined with a precise range of Cr eq /Ni eq ratios.
  • FIG. 1 which shows, seen in cross section, an austenitic stainless steel strip cast between rolls according to the prior art, and which demonstrates the morphology of the microcracks that it is desired to prevent;
  • FIG. 2 which is a curve showing the influence of the sulfur content of the metal on the presence of microcracks on the surface of the cast strip.
  • FIG. 1 shows a micrograph taken on a specimen of a thin austenitic stainless steel strip 1 , seen in longitudinal section.
  • This strip 1 has on its surface 2 a microcrack 3 of the type of those that the invention aims specifically to prevent.
  • the metallographic etching carried out in the specimen reveals a light area 4 located around the microcrack 3 and along its extension: it corresponds to a segregated region enriched with certain elements such as nickel and manganese.
  • any irregularity in these thicknesses is manifested by a high propensity of the cast strip to exhibit microcracks on its surface.
  • a regular thickness of the columnar part of the solidified shell which is the indicator that the level of the meniscus has varied only a little during casting, goes hand in hand with the absence of microcracks at the surface of the strip.
  • the curve in FIG. 2 shows the results of these investigations, which were made on strip 3 mm in thickness cast at a rate of 50 m/min.
  • the surfaces of the casting rolls were roughened by touching dimples having a mean depth of 80 ⁇ m and a mean diameter of 1000 ⁇ m.
  • the composition of the cast steels fell within the following limits: C: 0.0240-0.06%; Mn: 1.3-1.6%; P: 0.0190-0.024%; Si: 0.344-0.45%; Cr 18.0-18.7%; Ni: 8.6-9.8%; S: 0.0005-0.446%.
  • the CR eq /Ni eq ratios of these steels varied from 1.79 to 1.85.
  • the inert gas surrounding the meniscus contained 60% nitrogen by volume and 40% argon by volume.
  • Plotted on the x-axis is the sulfur content of the metal and plotted on the y-axis is an index representative of the magnitude of the fluctuations in the meniscus level during casting, which represents the standard deviation on the thickness of the columnar regions observed in the solidification structure of the strip. It may be seen that, for the same casting conditions, the higher the sulfur content of the metal, while moreover the contents of the other elements remain similar, the smaller the amplitude of the fluctuations in the level of the meniscus. Above a sulfur content of 0.007%, this influence decreases very significantly, whereas it remains very pronounced for the lower contents. It should also be realized that the presence of microcracks at the surface of the strip is directly related to these fluctuations and that the lower limit of 0.007% for the sulfur content also corresponds to the minimum needed to prevent the formation of microcracks.
  • the inventors have determined a set of conditions to be met so that the casting of austenitic stainless steels as thin strip takes place without the formation of microcracks at the surface of the strip, these conditions having been mentioned above. They are justified by the following considerations.
  • the sulfur content is less than 0.007%, the fluctuations in the level of the meniscus become too large and the irregularities in heat transfer which result therefrom cause the formation of microcracks, in particular when the CR eq /Ni eq ratio is greater than 1.70.
  • the upper limit of the sulfur content is set at 0.04% because above this value the influence of the sulfur content on the stability of the meniscus no longer increases significantly and, on the other hand, there is an increase in the risk of degrading the pitting corrosion resistance of the finished product manufactured from this strip.
  • the phosphorus content must be kept at less than 0.04% so as to avoid the risk of hot cracking of the strip when the CR eq /Ni eq ratio is close to 1.55, that is to say when solidification takes place partially as primary austenite and not predominantly as primary ferrite.
  • the Cr eq /Ni eq ratio must be at least 1.55, as below this value the steel solidifies at least partially as primary austenite, thereby increasing the cracking sensitivity of the strip and promoting the appearance of longitudinal cracks, which must also be absolutely prevented.
  • a Cr eq /Ni eq ratio greater than 1.90 the contraction owing to the ferrite-austenite transformation becomes too great and microcracks are then inevitable.
  • the ferrite content of the strip becomes too high, which may result in fractures after the operation of forming the finished products produced from the strip thus cast.
  • the other analytical conditions on the cast steel are conventional with regard to the most common austenitic stainless steels, especially those of the 304 and similar type.
  • elements other than those explicitly mentioned in the foregoing may be present in the steel as impurities or as alloying elements in small amounts, provided that they do not appreciably modify the solidification conditions and the surface tension of the liquid steel at the surface of the rolls, which would be confirmed by the absence of microcracks on the strip produced.
  • the nature of the inert gas surrounding the meniscus has a strong influence on the conditions under which the steel is in contact with the surface of the rolls, especially on the way in which the transfer takes place “as a negative” of the roughness of the rolls on the surface of the strip, and on the risk of forming microcracks.
  • a gas completely or predominantly insoluble in the steel such as argon or helium
  • Heat extraction therefore takes place practically only right at the roughness peaks, which makes the extraction very heterogeneous on the surface of the roll. This heterogeneity is conducive to the formation of numerous microcracks.
  • the steel penetrates well into the depressions in the surface of the rolls and heat extraction upon first contact is significant. In addition, this reduces the heterogeneity in the heat extraction right at the peaks and the depressions. All this goes toward limiting the risk of forming microcracks.
  • the lower limit of the content in the inert gas of a gas (or gas mixture) soluble in the steel is set at 50%.
  • Austenitic stainless steel strip 3 mm in thickness was cast between rolls. The surfaces of the rolls had touching dimples with a mean diameter of 1000 ⁇ m and a mean depth of 100 ⁇ m.
  • the inert gas surrounding the meniscus contained 40% argon and 60% nitrogen.
  • the composition of the steel varied within the following limits: C: 0.02-0.06%; Mn: 1.3-1.6%; P: 0.019-0.024%; Si: 0.34-0.45%; Cr: 18.0-18.7%; Ni: 8.6-9.8%; S: 0.0005-0.0446%.
  • the Cr eq/Ni eq ratio of the steels cast varied from 1.79 to 1.85.
  • the surface density of the microcracks on the strip thus cast was measured and the results of these measurements were compared with the sulfur contents in the steels cast. Table 1 gives the conclusions of these trials.
  • Austenitic stainless steel strip 3.8 mm in thickness was cast between rolls, the compositions of each steel being given in table 2.
  • the rolls had surface roughnesses characterized by the presence of touching dimples having a mean diameter of 1000 ⁇ m and a mean depth of 120 ⁇ m.
  • Table 3 Influence of the composition of the inert gas on the surface density of the microcracks on the strip, according to the sulfur content and the CR eq /Ni eq ratio of the steel cast.
  • composition of the inert gas is a parameter which it is often desirable to vary in order to control the intensity of the heat transfer between the rolls and the metal, for example in order to vary the crown of the rolls which affects the shape of the strip (see document EP-A-0 736 350).
  • the results obtained with steel C therefore lead to the conclusion that a sulfur content of 0.005% cannot fall within the scope of the invention.
  • the nitrogen content of the inert gas is at least 50%.
  • Their sulfur contents are 0.019 and 0.039% respectively and their Cr eq /Ni eq ratios are 1.82 and 1.64 respectively.
  • the invention preferably applies to the case of steels having a CR eq /Ni eq ratio of between 1.70 and 1.90 since this range corresponds to steels in which a lesser amount of gammagenic elements (such as nickel) has been added than in the case of steels having a lower Cr eq /Ni eq ratio, and which are therefore more economical to manufacture.

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Chemical & Material Sciences (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Continuous Casting (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Metal Extraction Processes (AREA)
  • Heat Treatment Of Articles (AREA)
  • Pressure Welding/Diffusion-Bonding (AREA)
  • Heat Treatment Of Steel (AREA)
US09/959,210 1999-04-22 2000-04-12 Method for continuously casting between two rolls austenitic stainless steel strips with excellent surface quality and resulting strips Expired - Lifetime US6739383B1 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR9905052A FR2792560B1 (fr) 1999-04-22 1999-04-22 Procede de coulee continue entre cylindres de bandes d'acier inoxydable austenitique d'excellente qualite de surface, et bandes ainsi obtenues
PCT/FR2000/000780 WO2000064612A1 (fr) 1999-04-22 2000-04-12 Procede de coulee continue entre cylindres de bandes d'acier inoxydable austentique d'excellente qualite de surface, et bandes ansi obtenues

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Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20070181284A1 (en) * 2003-10-21 2007-08-09 Thyssenkrupp Nirosta Gmbh Method for the production of cast steel strip
US20090047536A1 (en) * 2007-08-13 2009-02-19 Nucor Corporation Thin cast steel strip with reduced microcracking
US20090145567A1 (en) * 2007-10-12 2009-06-11 Nucor Corporation Method of forming textured casting rolls with diamond engraving
CN103255352A (zh) * 2013-04-19 2013-08-21 山西太钢不锈钢股份有限公司 一种超低碳奥氏体不锈钢棒材中提高形成奥氏体的方法
US8893768B2 (en) 2011-11-17 2014-11-25 Nucor Corporation Method of continuous casting thin steel strip
US9731345B2 (en) 2010-12-27 2017-08-15 Posco Martensitic stainless steel highly resistant to corrosion, and method for manufacturing same

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CN100493745C (zh) * 2006-06-23 2009-06-03 宝山钢铁股份有限公司 双辊薄带连铸方法
DE102007003548B3 (de) 2007-01-24 2008-09-04 Thyssenkrupp Nirosta Gmbh Gießwalze für eine Zweiwalzengießvorrichtung und Zweiwalzengießvorrichtung
KR101360660B1 (ko) * 2011-12-27 2014-02-07 주식회사 포스코 에지 품질이 우수한 오스테나이트계 스테인리스 강판의 제조방법
KR101510506B1 (ko) 2012-12-26 2015-04-08 주식회사 포스코 스컴의 생성을 저감시킨 쌍롤식 박판 주조 방법
JP6347864B1 (ja) * 2017-03-24 2018-06-27 日新製鋼株式会社 オーステナイト系ステンレス鋼スラブの製造方法
CN107030264B (zh) * 2017-04-27 2019-04-26 酒泉钢铁(集团)有限责任公司 一种超级奥氏体不锈钢双辊薄带铸轧生产工艺
CN109778077B (zh) * 2017-11-10 2021-01-08 大连华锐重工集团股份有限公司 一种核主泵泵壳材料的冶炼方法
US20200406321A1 (en) 2018-03-02 2020-12-31 Nippon Steel Corporation Manufacturing method for slab and continuous casting equipment
CN108239724A (zh) * 2018-03-29 2018-07-03 冯满 一种合金钢

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Publication number Priority date Publication date Assignee Title
US5807444A (en) * 1996-03-22 1998-09-15 Usinor Sacilor Process for the continuous casting of an austenitic stainless steel strip onto one or between two moving walls with dimpled surfaces, and casting plant for its implementation

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5103895A (en) * 1989-07-20 1992-04-14 Nippon Steel Corporation Method and apparatus of continuously casting a metal sheet
EP0679114B2 (en) * 1993-11-18 2004-11-03 Castrip, LLC Casting stainless steel strip on surface with specified roughness

Patent Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5807444A (en) * 1996-03-22 1998-09-15 Usinor Sacilor Process for the continuous casting of an austenitic stainless steel strip onto one or between two moving walls with dimpled surfaces, and casting plant for its implementation

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20070181284A1 (en) * 2003-10-21 2007-08-09 Thyssenkrupp Nirosta Gmbh Method for the production of cast steel strip
US20090047536A1 (en) * 2007-08-13 2009-02-19 Nucor Corporation Thin cast steel strip with reduced microcracking
US7975754B2 (en) 2007-08-13 2011-07-12 Nucor Corporation Thin cast steel strip with reduced microcracking
US20090145567A1 (en) * 2007-10-12 2009-06-11 Nucor Corporation Method of forming textured casting rolls with diamond engraving
US8122937B2 (en) 2007-10-12 2012-02-28 Nucor Corporation Method of forming textured casting rolls with diamond engraving
US9731345B2 (en) 2010-12-27 2017-08-15 Posco Martensitic stainless steel highly resistant to corrosion, and method for manufacturing same
US8893768B2 (en) 2011-11-17 2014-11-25 Nucor Corporation Method of continuous casting thin steel strip
CN103255352A (zh) * 2013-04-19 2013-08-21 山西太钢不锈钢股份有限公司 一种超低碳奥氏体不锈钢棒材中提高形成奥氏体的方法

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ATE229391T1 (de) 2002-12-15
KR100636868B1 (ko) 2006-10-19
EP1185387B1 (fr) 2002-12-11
CZ20013776A3 (cs) 2002-03-13
TR200103014T2 (tr) 2002-03-21
CZ296650B6 (cs) 2006-05-17
FR2792560B1 (fr) 2001-06-01
FR2792560A1 (fr) 2000-10-27
DE60000997T2 (de) 2003-07-17
RU2239518C2 (ru) 2004-11-10
CN1187148C (zh) 2005-02-02
JP2002542039A (ja) 2002-12-10
AU767990B2 (en) 2003-11-27
KR20010113824A (ko) 2001-12-28
DK1185387T3 (da) 2003-03-24
TW434058B (en) 2001-05-16
SK14602001A3 (sk) 2002-05-09
ZA200108666B (en) 2004-06-30
SK286180B6 (sk) 2008-04-07
EP1185387A1 (fr) 2002-03-13
SI1185387T1 (en) 2003-04-30
CN1351528A (zh) 2002-05-29
DE60000997D1 (de) 2003-01-23
WO2000064612A1 (fr) 2000-11-02
JP4454868B2 (ja) 2010-04-21
AU3661800A (en) 2000-11-10
ES2188523T3 (es) 2003-07-01
BR0009894A (pt) 2002-01-15
PT1185387E (pt) 2003-04-30
PL194231B1 (pl) 2007-05-31
PL351566A1 (en) 2003-05-05

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